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WO2017111467A1 - Acier inoxydable austénitique ayant une aptitude à la transformation améliorée - Google Patents

Acier inoxydable austénitique ayant une aptitude à la transformation améliorée Download PDF

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Publication number
WO2017111467A1
WO2017111467A1 PCT/KR2016/015024 KR2016015024W WO2017111467A1 WO 2017111467 A1 WO2017111467 A1 WO 2017111467A1 KR 2016015024 W KR2016015024 W KR 2016015024W WO 2017111467 A1 WO2017111467 A1 WO 2017111467A1
Authority
WO
WIPO (PCT)
Prior art keywords
stainless steel
less
austenitic stainless
excluding
work hardening
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Ceased
Application number
PCT/KR2016/015024
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English (en)
Korean (ko)
Inventor
강형구
최점용
채동철
유지현
조규진
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Posco Holdings Inc
Original Assignee
Posco Co Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Posco Co Ltd filed Critical Posco Co Ltd
Priority to CN201680070348.5A priority Critical patent/CN108291289B/zh
Priority to MYPI2018000974A priority patent/MY189629A/en
Priority to EP16879334.7A priority patent/EP3396001B1/fr
Priority to JP2018529145A priority patent/JP6796134B2/ja
Priority to US16/065,710 priority patent/US20190010588A1/en
Publication of WO2017111467A1 publication Critical patent/WO2017111467A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese

Definitions

  • the present invention relates to an austenitic stainless steel with improved workability, and more particularly, to an austenitic stainless steel with improved workability in which defects such as delayed fracture do not occur even when processed into a complicated shape.
  • the present invention relates to stainless steel used in sink bowls and the like, and more particularly, to stainless steel having excellent workability such that delayed fracture does not occur in processing into a sink bowl.
  • Sink bowls for kitchen sinks are usually made of stainless steel. Usually, general purpose stainless steels are used. In general, the shape of the sink bowl is widely used because there is no problem in formability.
  • FIG. 1 is a photograph of the corner portion after the sink bowl processing with a conventional austenitic stainless steel.
  • Delayed fracture occurs after a certain time after processing of the steel sheet, and occurs mainly in the part where the processing amount is large depending on the processed shape.
  • austenitic stainless steel is highly workable, but delayed fracture of aging crack occurs when the processing rate exceeds the limit. These cracks occur after a few months after the deep drawing processing of the austenitic stainless steel, and proceed linearly in the deep drawing direction, but microscopically, they proceed in a zigzag form regardless of the grain boundaries of the austenitic stainless steel.
  • the present invention is to provide a method for producing stainless steel excellent in workability that does not occur defects such as delayed destruction even when processing into such a complicated shape.
  • Patent Document 0001 Korean Laid-Open Patent Publication No. 10-2014-0131214
  • Embodiments of the present invention provide an austenitic stainless steel pipe having excellent workability to prevent delayed fracture in processing into a sink bowl.
  • Austenitic stainless steel with improved workability in weight percent, silicon (Si): 0.1 to 0.65%, manganese (Mn): 0.2 to 3.0%, nickel (Ni): 6.5 to 10.0 %, Chromium (Cr): 16.5 to 20.0%, copper (Cu): 6.0% or less (excluding 0), carbon (C) + nitrogen (N): 0.08% or less (excluding 0), the rest is Fe and unavoidable It contains impurities and has a work hardening rate of 1500 MPa or less in the range of true strain 0.15 to 0.4.
  • carbon (C) + nitrogen (N): may include 0.05% or less (excluding 0).
  • carbon (C) + nitrogen (N): may include 0.03% or less (excluding 0).
  • the ASTM grain size may be 8 or less.
  • Embodiments of the present invention can prevent the occurrence of delayed fracture after molding, even in the corner portion with a large amount of processing in processing with a sink bowl using austenitic stainless steel, the true strain rate and the work hardening rate is controlled.
  • FIG. 1 is a photograph of the corner portion after the sink bowl processing with a conventional austenitic stainless steel.
  • Figure 2 is a photograph of the corner portion after the sink bowl processing austenitic stainless steel according to an embodiment of the present invention.
  • Figure 3 is a graph showing the correlation between the true strain rate and the work hardening rate of the austenitic stainless steel according to an embodiment of the present invention.
  • Austenitic stainless steel with improved workability in weight percent, silicon (Si): 0.1 to 0.65%, manganese (Mn): 0.2 to 3.0%, nickel (Ni): 6.5 to 10.0 %, Chromium (Cr): 16.5 to 20.0%, copper (Cu): 6.0% or less (excluding 0), carbon (C) + nitrogen (N): 0.08% or less (excluding 0), the rest is Fe and unavoidable It contains impurities and has a work hardening rate of 1500 MPa or less in the range of true strain 0.15 to 0.4.
  • Austenitic stainless steel with improved workability in weight percent, silicon (Si): 0.1 to 0.65%, manganese (Mn): 0.2 to 3.0%, nickel (Ni): 6.5 to 10.0 %, Chromium (Cr): 16.5 to 20.0%, copper (Cu): 6.0% or less (excluding 0), carbon (C) + nitrogen (N): 0.08% or less (excluding 0), the rest is Fe and unavoidable Contains impurities.
  • Silicon (Si) is added by adjusting in the range of 0.1 to 0.65% by weight.
  • Silicon (Si) is an element that is essentially added for the deoxidation, and because it is expensive in the steelmaking process to control the content in too low amount, it is limited to 0.1% or more.
  • Si is a solid solution strengthening element, which increases its strength and hardens the material.
  • the upper limit is limited to 0.65% because corrosion resistance is lowered by forming inclusions in combination with oxygen.
  • Manganese (Mn) is added by adjusting in the range of 0.2 to 3.0% by weight.
  • Manganese (Mn) is not only essential for deoxidation, but also increases the stabilization of austenite phase and reduces the amount of ferrite or martensite formation, and it is effective in reducing the work hardening rate. Therefore, 0.2% or more is added.
  • Mn is a solid solution strengthening element, and excessively high content of Mn may increase the strength of the steel, and lower the corrosion resistance of the material, so the upper limit thereof is limited to 3.0%.
  • Nickel (Ni) is added by adjusting in the range of 6.5 to 10.0% by weight.
  • Nickel (Ni) is not only effective in improving corrosion resistance such as corrosion resistance by adding chromium (Cr) in combination, but also increasing the content thereof, thereby reducing the rate of soft nitriding and work hardening of austenitic steel.
  • nickel (Ni) is an element that increases the degree of stabilization of the austenite phase and reduces the amount of ferrite or martensite produced in the steel pipe, and 6.5% or more is added to maintain the austenite balance.
  • Ni nickel
  • Chromium (Cr) is added in a controlled range of 16.5 to 20.0% by weight.
  • Chromium (Cr) is an essential element to improve the corrosion resistance of stainless steel, and more than 16.5% must be added to be used for general purposes.
  • Cr is a solid solution strengthening element, and an excessively high content of Cr causes an increase in cost, so the upper limit is limited to 20.0%.
  • Copper (Cu) is added in a controlled range of 6.0% by weight or less (excluding 0).
  • Copper (Cu) has the effect of reducing the rate of soft nitriding and work hardening of austenitic steel, and is an element that reduces the amount of ferrite or martensite produced in the steel, it is preferable to add it.
  • Carbon (C) + nitrogen (N) should be added at 0.08% by weight or less (excluding 0).
  • Carbon (C) and nitrogen (N) are not only hardening austenitic stainless steels as intrusion-type solid solution strengthening elements, but if their contents are high, they harden the strained organic martensite generated during processing to increase the work hardening of the material. Done.
  • the present invention limits the content of C + N to 0.08% or less.
  • the content of carbon (C) and nitrogen (N) may preferably be 0.05% or less (excluding 0), and more preferably, carbon (C) and nitrogen (N).
  • the content of may be 0.03% or less (excluding 0).
  • the austenitic stainless steel has a work hardening rate of 1,500 MPa or less in a true strain range of 0.15 to 0.4.
  • FIG. 2 is a photograph of the corner portion after the sink bowl processing austenitic stainless steel according to an embodiment of the present invention.
  • FIG. 2 shows that delayed fracture does not occur after molding even at the corners having a large amount of processing when the stainless steel manufactured by the method of the present invention is applied to the sink bowl processing having the shape as shown in FIG. 1.
  • Figure 3 is a graph showing the correlation between the true strain rate and the work hardening rate of the austenitic stainless steel according to an embodiment of the present invention.
  • Figure 3 shows the work hardening rate according to the true strain after the uniaxial tensile test of conventional stainless steel and stainless steel of the present invention.
  • Conventional stainless steel shows that the process hardening rate is increased more than 1,500 MPa in the true strain rate of 0.15 or more and 0.4 or less, while the stainless steel according to the present invention is maintained at 1,500 MPa or less.
  • machining of stainless steel causes work hardening. Since delayed fracture occurs when a large amount of processing occurs, the present invention examined the work hardening in the range of 0.15 or more and 0.4 or less in true strain.
  • Work hardening is quantitatively expressed as the work hardening rate, which is the ratio of the change of true stress to the change of true strain in stainless steel. Referring to Figure 3, it can be seen that in the stainless steel used in the prior art, the work hardening rate was 1,500 MPa or more in the range of true strain 0.15 or more and 0.4 or less.
  • the work hardening rate was calculated from the true strain and true stress values obtained by uniaxial tensile test until the fracture after processing the tensile test specimen according to JIS13B, JIS5 standards and the like.
  • Tensile specifications can be anything and are merely examples.
  • the delayed destruction can actually be processed into a sink bowl shape, and it can be seen after processing into a simple cup shape with a diameter of 50mm and a height of 100mm.
  • the ASTM grain size number of the stainless steel may be 8 or less.
  • the grain size is the grain size measured in the longitudinal section of the stainless steel pipe.
  • the stainless steel may have a ferrite phase fraction of less than 1%, and the stainless steel may have a martensite phase fraction of less than 1%. That is, the stainless steel has a ferrite or martensite fraction measured by the magnetization method of less than 1%.
  • the cold rolled steel sheet was used to process the sink bowl, and the work hardening rate of the steel sheet was measured.
  • the delayed fracture after the sink bowl was visually observed and shown in Table 2 below.
  • Table 1 and Table 2 show that the delayed fracture does not occur in the stainless steel prepared by adjusting the component range and work hardening rate proposed in the present invention.
  • two comparative examples of stainless steels used in the related art did not satisfy the processing hardening rate of 1,500 MPa or less under the same conditions, and it was found that delayed fracture occurred.
  • FIG. 1 is a photograph of the corner portion after the sink bowl processing with austenitic stainless steel according to Comparative Example 1
  • Figure 2 is a corner portion after the sink bowl processing with austenitic stainless steel according to Example 1
  • One picture. 3 is a graph showing the correlation between the true strain rate and the work hardening rate of the austenitic stainless steel according to Comparative Example 1 and the austenitic stainless steel according to Example 1 of the present invention.
  • Austenitic stainless steel according to embodiments of the present invention has industrial applicability applicable to sink bowls of kitchen sinks.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

L'invention concerne un acier inoxydable austénitique ayant une aptitude à la transformation améliorée. L'acier inoxydable austénitique selon l'invention comprend, en pourcentage en poids, 0,1 à 0,65 % de silicium (Si), 0,2 à 3,0 % de manganèse (Mn), 6,5 à 10,0 % de nickel (Ni), 16,5 à 20,0 % de chrome (Cr), 6,0 % ou moins (0 étant exclu) de cuivre (Cu), 0,08 % ou moins (0 étant exclu) de carbone (C) + azote (N) et le reste de Fe et d'impuretés inévitables, la vitesse d'écrouissage étant inférieure ou égale à 1500 MPa dans une plage d'allongement réel de 0,15 à 0,4. Ainsi, lors de la formation d'un évier, etc. à l'aide de l'acier inoxydable austénitique ayant l'allongement réel et la vitesse d'écrouissage réglée s'y rapportant, l'apparition d'une fracture retardée après moulage peut être évitée, même pour des sections de bord sur lesquelles un plus grand degré de transformation est appliqué.
PCT/KR2016/015024 2015-12-23 2016-12-21 Acier inoxydable austénitique ayant une aptitude à la transformation améliorée Ceased WO2017111467A1 (fr)

Priority Applications (5)

Application Number Priority Date Filing Date Title
CN201680070348.5A CN108291289B (zh) 2015-12-23 2016-12-21 具有改善的可加工性的奥氏体不锈钢
MYPI2018000974A MY189629A (en) 2015-12-23 2016-12-21 Austenitic stainless steel having improved processability
EP16879334.7A EP3396001B1 (fr) 2015-12-23 2016-12-21 Acier inoxydable austénitique ayant une aptitude à la transformation améliorée
JP2018529145A JP6796134B2 (ja) 2015-12-23 2016-12-21 加工性が向上したオーステナイト系ステンレス鋼
US16/065,710 US20190010588A1 (en) 2015-12-23 2016-12-21 Austenitic stainless steel having improved processability

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
KR10-2015-0184668 2015-12-23
KR1020150184668A KR101756701B1 (ko) 2015-12-23 2015-12-23 가공성이 향상된 오스테나이트계 스테인리스강

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WO2017111467A1 true WO2017111467A1 (fr) 2017-06-29

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PCT/KR2016/015024 Ceased WO2017111467A1 (fr) 2015-12-23 2016-12-21 Acier inoxydable austénitique ayant une aptitude à la transformation améliorée

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US (1) US20190010588A1 (fr)
EP (1) EP3396001B1 (fr)
JP (1) JP6796134B2 (fr)
KR (1) KR101756701B1 (fr)
CN (1) CN108291289B (fr)
MY (1) MY189629A (fr)
WO (1) WO2017111467A1 (fr)

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KR102268906B1 (ko) * 2019-07-17 2021-06-25 주식회사 포스코 강도가 향상된 오스테나이트계 스테인리스강 및 그 제조 방법
JP7576935B2 (ja) * 2020-07-06 2024-11-01 日鉄ステンレス株式会社 非磁性ステンレス鋼板および機械部品用鋼材の製造方法
KR20220169655A (ko) * 2021-06-21 2022-12-28 주식회사 포스코 오스테나이트계 스테인리스강 및 그 제조방법
CN118460926B (zh) * 2024-05-21 2025-11-21 山西太钢不锈钢股份有限公司 一种易加工高硬化奥氏体不锈钢及其制造方法

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See also references of EP3396001A4

Also Published As

Publication number Publication date
JP2019501289A (ja) 2019-01-17
EP3396001B1 (fr) 2021-09-22
KR101756701B1 (ko) 2017-07-12
CN108291289A (zh) 2018-07-17
US20190010588A1 (en) 2019-01-10
CN108291289B (zh) 2020-10-02
EP3396001A4 (fr) 2019-01-23
MY189629A (en) 2022-02-22
JP6796134B2 (ja) 2020-12-02
KR20170075840A (ko) 2017-07-04
EP3396001A1 (fr) 2018-10-31

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